Aluminum nitride ceramics, members for use in a system for producing semiconductors, and corrosion resistant members

ABSTRACT

It is an object of the present invention to increase the volume resistivity of an aluminum nitride ceramics. An aluminum nitride ceramics contains 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms and having a volume resistivity at room temperature of not lower than 1×10 14  Ω·cm. Alternatively, the ceramics has a volume resistivity at 500° C. of not lower than 1×10 8  Ω·cm. Alternatively, an aluminum nitride ceramics has an a-axis lattice constant of aluminum nitride not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride not shorter than 4.980 angstrom.

[0001] This application claims the benefits of Japanese Patent Applications P2001-358971 filed on Nov. 26, 2001 and P2002-290683 filed on Oct. 3, 2002, the entireties of which are incorporated by reference.

BACKGROUND OF THE INVENTION

[0002] 1. Field of the Invention

[0003] The present invention relates to an aluminum nitride series ceramics having a high volume resistivity and a member for a system for producing semiconductors and an corrosion resistant member applying such ceramics.

[0004] 2. Related Art Statement

[0005] An aluminum nitride sintered body has an corrosion resistant property against a halogen gas and has thus been utilized as a base material of various members for a system for producing semiconductors. It is further needed that a base material for a ceramic heater has a specified insulating property and thermal conductivity in an operating temperature range. An aluminum nitride sintered body has an insulating property and a high thermal conductivity and thus has been utilized as a base material for a ceramic heater for heating silicon wafers. A dense aluminum nitride sintered body usually has a volume resistivity of about 10¹³ Ω·cm at room temperature, for example, and not higher than 10⁷ Ω·cm at 500° C. It has been thus demanded an aluminum nitride sintered body having a volume resistivity of, for example, not lower than 10⁸ Ω·cm at 500° C.

[0006] The assignee filed Japanese patent publication 2000-44345A and disclosed a novel method of producing an aluminum nitride sintered body. In the disclosure, a magnesium component is added to raw material of aluminum nitride powder to provide a sintered body having a high corrosion resistant property and volume resistivity.

SUMMARY OF THE INVENTION

[0007] Magnesium is, however, an alkaline earth metal element and has been considered to be not desirable in a semiconductor production process. In addition, it may be difficult to give a solution for a process carried out at a higher temperature range by the above method using a magnesium component.

[0008] An object of the present invention is to increase the volume resistivity of an aluminum nitride ceramics.

[0009] Another object of the present invention is to increase the volume resistivity in a high temperature range of an aluminum nitride ceramics so as to improve the insulating property in a high temperature range.

[0010] The present invention provides an aluminum nitride ceramics containing 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms and having a volume resistivity at room temperature of not lower than 1×10¹⁴ Ω·cm.

[0011] The present invention further provides an aluminum nitride ceramics containing 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms and having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.

[0012] The present invention further provides an aluminum nitride ceramics wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.

[0013] The present invention further provides an aluminum nitride ceramics produced by sintering a mixture containing at least aluminum nitride and boron carbide and having a volume resistivity at room temperature of not lower than 1×10¹⁴ Ω·cm.

[0014] The present invention further provides an aluminum nitride ceramics produced by sintering a mixture containing at least aluminum nitride and boron carbide and having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.

[0015] The present invention provides a member comprising at least the aluminum nitride ceramics for use in a system for producing semiconductors.

[0016] The present invention further provides an corrosion resistant member comprising the aluminum nitride ceramics.

[0017] The inventors have tried to add various additives to an aluminum nitride ceramics and studied the effects of the additives on the volume resistivity at room temperature and a high temperature range. They have reached the following findings. That is, the volume resistivity of an aluminum nitride ceramics may be increased to a value not lower than 1×10¹⁴ Ω·cm at room temperature by adding a predetermined amount of boron carbide into raw material of the sintered body. Further, they found that the volume resistivity at 500° C. may be increased to a value not lower than 1×10⁸ Ω·cm, so that excellent insulating property may be obtained at a high temperature range. The present invention is based on the findings.

[0018] The inventors further investigated requirements of an aluminum nitride ceramics for enabling an increase of the volume resistivity. They have found that relatively large amounts of carbon and oxygen atoms are solid-soluted in aluminum nitride grains, as described in a section of “examples”. Therefore, carbon and oxygen atoms are solid-soluted in aluminum nitride grains to increase the resistivity of the aluminum nitride ceramics.

[0019] The inventors have measured the lattice constants of aluminum nitride by X-ray diffraction measurement based on such theory. It was finally found that the volume resistivity of the ceramics may be improved by increasing the a-axis and c-axis lattice constants of aluminum nitride to predetermined critical values. The results show that the crystalline lattices of aluminum nitride are enlarged as carbon and oxygen atoms are solid- soluted in the lattices.

[0020] That is, according to the present invention, the a-axis lattice constant is made not lower than 3.112 angstrom and c-axis lattice constant is made not lower than 4.980 angstrom.

[0021] The intergranular phase of aluminum nitride series ceramics having an increased volume resistivity was mainly boron nitride (BN). The intergranular phase is substantially plate-shaped and elongated along the interface of adjacent aluminum nitride grains, and forms an isolated phase (dispersed phase) between the aluminum nitride grains. The intergranular phase does not substantially affect the volume resistivity of an aluminum nitride ceramics.

[0022] In a sintering step, the following process may proceed. Boron carbide reacts with gaseous nitrogen to generate boron nitride as an intergranular phase, and carbon atoms are diffused and solid-soluted in aluminum nitride grains. Oxygen atoms present in raw material of aluminum nitride may be solid-soluted into the aluminum nitride grains at the same time.

[0023] The inventors has added boron nitride powder into powdery raw material of aluminum nitride and sintered. In this case, intergranular phase mainly consisting of boron nitride is formed along the interface of aluminum nitride grains. It was not, however, observed an increase of volume resistivity due to carbon and oxygen atoms solid-soluted into aluminum nitride grains.

[0024] Further, the inventors have tried to add carbon powder into powdery raw material of aluminum nitride so as to diffuse carbon atoms into aluminum nitride grains. In this case, however, carbon atoms dissipate or remain in the intergranular phase. An amount of carbon atoms solid-soluted into aluminum nitride grains is small and insufficient for enlarging the crystalline lattice of aluminum nitride. The observation supports the following theory. That is, boron carbide and gaseous nitrogen are reacted to generate highly active carbon atoms, which are diffused into aluminum nitride grains.

[0025] Further, in Japanese patent publication P5-178, 671A, boron carbide (B₄C) in an amount of 0.5 weight percent calculated as boron is added into aluminum nitride powder and the powder is then sintered at 1800° C. It is thus obtained a sintered body having a thermal conductivity of 153 W/m·K and a relative density of 98.9 percent. Boron carbide is added for inhibiting the crystalline growth and improving the surface smoothness. The relationship between the addition of boron carbide and volume resistivity is not described. According to the study of the inventors, in the case of adding such small amount of boron carbide, solid solution of carbon and oxygen atoms into aluminum nitride grains does not substantially affect the lattice constants and the volume resistivity of the aluminum nitride ceramics.

[0026] These and other objects, features and advantages of the invention will be appreciated upon reading the following description of the invention when taken in conjunction with the attached drawings, with the understanding that some modifications, variations and changes of the same could be made by the skilled person in the art.

BRIEF DESCRIPTION OF THE DRAWINGS

[0027]FIG. 1 is a graph showing the temperature dependence of the volume resistivity in samples according to examples 1, 3 and comparative example 1.

[0028]FIG. 2 shows distribution of B, C, O, N and Y atoms in a sample of example 1 taken by EPMA.

[0029]FIG. 3 shows distribution of B, C, O, N and Y atoms in a sample of comparative example 5 taken by EPMA.

[0030]FIG. 4 shows distribution of a-axis and c-axis lattice constants of inventive and comparative examples.

PREFERRED EMBODIMENTS OF THE INVENTION

[0031] The present invention will be described further in detail.

[0032] An aluminum nitride ceramics according to the present invention means a ceramic material mainly consisting of a polycrystalline body composed of aluminum nitride. The ceramics may be produced by a process not particularly limited, including a gaseous phase process such as chemical vapor deposition, physical vapor deposition, organic metal chemical vapor deposition and vapor deposition. An aluminum nitride ceramics may preferably be produced by sintering.

[0033] The content of aluminum in the aluminum nitride ceramics should be enough for forming aluminum nitride phase as the main phase. The content may preferably be not lower than 35 weight percent, and more preferably be not lower than 50 weight percent, of the aluminum nitride ceramics.

[0034] The content of aluminum nitride may preferably be not lower than 80 weight percent and more preferably be not lower than 90 weight percent in an aluminum nitride ceramics.

[0035] The resistivity of aluminum nitride ceramics may be further improved by increasing the content of boron atoms to a value not lower than 0.5 weight percent and the content of carbon atoms to a value not lower than 0.1 weight percent in an aluminum nitride series ceramics. On this viewpoint, the content of boron atoms may preferably be not lower than 0.8 weight percent, or the content of carbon atoms may preferably be not lower than 0.3 weight percent.

[0036] The thermal conductivity of an aluminum nitride ceramics may be further increased by reducing the content of boron atoms to a value not higher than 10 weight percent. On this viewpoint, the content of boron atoms may preferably be not higher than 5 weight percent. Moreover, the thermal conductivity of an aluminum nitride ceramics may be increased by reducing the content of carbon atoms to a value not higher than 2.5 weight percent. On this viewpoint, the content of carbon atoms may preferably be not higher than 1.5 weight percent.

[0037] In a preferred embodiment, the ratio of the contents (by weight) of carbon atoms to boron atoms (C/B) is controlled at a value not lower than 0.1 and not higher than 0.5. It is thereby possible to further increase the volume resistivity of an aluminum nitride series ceramics.

[0038] According to the present invention, the volume resistivity at room temperature of an aluminum nitride series ceramics may be made 1×10¹⁴ Ω·cm or higher. The volume resistivity at room temperature may be not lower than 5×10¹⁴ Ω·cm and further not lower than 1×10¹⁵ Ω·cm.

[0039] Further in the present invention, the volume resistivity at 500° C. of an aluminum nitride series ceramics may be made not lower than 1×10⁸ Ω·cm. Further, the volume resistivity at 500° C. may be not lower than 5×10⁸ Ω·cm.

[0040] Further in the present invention, the volume resistivity at 700° C. of an aluminum nitride series ceramics may be made not lower than 1×10⁷ Ω·cm. Further, the volume resistivity at 700° C. may be more preferably not lower than 5×10⁷ Ω·cm.

[0041] In a preferred embodiment, a-axis lattice constant of an aluminum nitride is not lower than 3.112 angstrom and c-axis lattice constant is not lower than 4.980 angstrom. It is thereby possible to increase the volume resistivity of an aluminum nitride series ceramics. On this viewpoint, the a-axis lattice constant may preferably be not lower than 3.113 angstrom, or, c-axis lattice constant may preferably be not lower than 4.981 angstrom.

[0042] An aluminum nitride ceramics according to the present invention, particularly sintered body, may preferably contain a rare earth element in an amount of 0.1 to 10 weight percent. It is thereby possible to obtain a higher volume resistivity at a lower sintering temperature compared with the ceramics with no rare earth element added. On this viewpoint, the content of a rare earth element may preferably be not lower than 0.2 weight percent and be not higher than 8 weight percent. The addition of a rate earth element is also effective for improving the thermal conductivity.

[0043] The rare earth element refers to the following seventeen elements; samarium, scandium, yttrium, lanthanum, cerium, praseodymium, neodymium, promethium, europium, gadolinium, terbium, dysprosium, holmium, erbium, thulium, ytterbium and lutetium.

[0044] In a preferred embodiment, the rare earth element is one or more element selected from the group consisting of yttrium, lanthanum, cerium, neodymium, samarium, gadolinium, dysprosium, erbium and ytterbium.

[0045] For providing a highly corrosive resistant sintered body suited for applications in which the contamination of impurities is to be highly controlled (such as an application for producing semiconductors), the total content of metal elements (excluding aluminum and rare earth elements) may preferably be not higher than 100 ppm, in some cases. The total content may more preferably be not higher than 50 ppm.

[0046] In a preferred embodiment, the open porosity of an aluminum nitride series ceramics is not higher than 5 percent and more preferably be not higher than 0.1 percent.

[0047] In a preferred embodiment, the thermal conductivity of an aluminum nitride series ceramics according to the present invention is not lower than 30 W/m·K. The upper limit of the thermal conductivity is not limited and may be 150 W/m·K for example.

[0048] In a preferred embodiment, an aluminum nitride series ceramics contains intergranular phase mainly consisting of boron nitride. The following crystalline phases may be generated other than boron nitride phase.

[0049] (1) A composite oxide phase of a rare earth element and aluminum. The composite oxide phase may preferably have garnet or perovskite crystalline structure.

[0050] (2) A boride of a rare earth element.

[0051] The inventors have found that the volume resistivities at room and high temperatures of an aluminum nitride ceramics may be further increased by controlling the ratio (a/b) of an oxygen content (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in the ceramics at a value not lower than 0.25 and not higher than 2.0. (a/b) may preferably be not lower than 0.4 and more preferably not lower than 0.5 for further increasing the volume resistivities at room and high temperatures of the ceramics. Alternatively, (a/b) may preferably be not higher than 1.8 and more preferably be not higher than 1.5.

[0052] (a/b) may be adjusted by controlling the oxygen content in raw material of aluminum nitride and an added amount of boron carbide into the raw material.

[0053] The inventors have further found that the thermal conductivity of an aluminum nitride ceramics may be considerably improved by reducing the oxygen content in aluminum nitride grains solid-soluted to a value not higher than 0.5 weight percent. It is thereby possible to increase the thermal conductivity of an aluminum nitride ceramics to a value not lower than 90 W/mK and more preferably not lower than 100 W/mK.

[0054] For further improving the thermal conductivity of an aluminum nitride series ceramics, the content of the solid-soluted oxygen may preferably be not higher than 0.4 weight percent and more preferably be not higher than 0.3 weight percent.

[0055] Raw material of aluminum nitride may be produced by various processes, including direct nitriding, reduction nitriding and gaseous phase synthesis from an alkyl aluminum.

[0056] Boron carbide may be added to raw material of aluminum nitride. When a rare earth element is added, the oxide of the rare earth element may be added to the raw material of aluminum nitride. Alternatively, the compound of the rare earth element forming a rare earth oxide upon heating (a precursor of a rare earth element) may be added to raw material of aluminum nitride. The precursor includes a nitrate, sulfate, oxalate and alkoxide. The precursor may be added as powder. The precursor such as a nitrate or sulfate may be dissolved into a solvent to obtain solution, which may be added into the raw material. It is thereby possible to uniformly disperse atoms of the rare earth element between aluminum nitride particles by dissolving the precursor in a solvent.

[0057] The raw material may be shaped by any known methods including dry press, doctor blade, extrusion, casting and tape forming methods.

[0058] In a formulating step, raw powder of aluminum nitride may be dispersed in a solvent, into which the rare earth element and boron carbide may be added in a form of powder or the solution described above. In a mixing step, it is possible to simply stir the powder. When the raw powder contains aggregates, it is possible to use a mixing and pulverizing machine, such as a pot mill, trommel and attrition mill, for pulverizing the aggregates. When using an additive soluble in a solvent for pulverizing, it is enough to carry out the mixing and pulverizing step for a short (minimum) time. Further, a binder component, such as polyvinyl alcohol, may be added.

[0059] The solvent used for the mixing step may be dried, preferably by spray dry method. After carrying out vacuum drying process, the particle size distribution of the dried mixtures may preferably be adjusted by passing the particles through a mesh.

[0060] In a forming step of the powdery material, the material may be pressed using a metal mold to provide a disk-shaped body. The pressure for pressing raw material is not particularly limited, as long as the shaped body may be handled without causing any fracture. The pressure may preferably be not lower than 100 kgf/cm². The powdery material may be contained in a die for hot pressing without particularly shaping the powdery material.

[0061] The sintered body according to the invention may preferably be produced by hot pressing a body to be sintered, preferably at a pressure of not lower than 50 kgf/cm².

[0062] The sintering temperature is not limited, and may preferably be 1700 to 2200° C. and more preferably be not lower than 1750° C. or not higher than 2100° C. The sintering temperature may most preferably be 1750 to 2050° C.

[0063] In a sintering step, the temperature may preferably be held at a holding temperature between 1400 to 1700° C. before sintering at a maximum temperature to further improve the thermal conductivity of the ceramics.

[0064] The aluminum nitride ceramics according to the invention may preferably be used for various members in a system for producing semiconductors, such as systems for treating silicon wafers and for manufacturing liquid crystal displays. Such system for producing semiconductors means a system usable in a wide variety of semiconductor processes in which metal contamination of a semiconductor is to be avoided. Such system includes a film forming, etching, cleaning and testing systems.

[0065] An aluminum nitride series ceramics according to the invention may be used as an corrosion resistant member. The corrosion resistant member may be used against corrosive substances such as a liquid including nitric acid, hydrochloric acid, mixed acid, hydrofluoric acid and aqua regia. The corrosive substance further includes a chlorine-based corrosive gas such as Cl₂, BCl₃, ClF₃, HCl or the like and a fluorine-based corrosive gas such as ClF₃ gas, NF₃ gas, CF₄ gas, WF₆, SF₄ or the like. The corrosive resistant member is particularly useful against the plasma of each gas.

[0066] The member for a system for producing semiconductors may preferably be a corrosion resistant member such as a susceptor for the system. The inventive ceramics may be preferred for a metal-embedded article having an anti-corrosion member and a metal member embedded therein. The corrosion resistant member includes a susceptor for mounting a semiconductor wafer thereon, a dummy wafer, a shadow ring, a tube for generating high frequency plasma, a dome for generating high frequency plasma, a high frequency wave-permeable window, an infrared radiation-permeable window, a lift pin for supporting a semiconductor wafer, a shower plate, an electrostatic chuck and a vacuum chuck. A resistive heating element, electrostatic chuck electrode or an electrode for generating high frequency plasma may be provided in the susceptor.

[0067] The aluminum nitride ceramics according to the present invention has a high volume resistivity at a high temperature as described above. The ceramics may be thus particularly useful for a ceramic heater designed for use in a high temperature range. Such ceramic heater may be appropriately used under a maximum temperature of, for example, 1000° C.

[0068] Further, the aluminum nitride ceramics according to the invention has a relatively high volume resistivity of about 10⁷ to 10⁹ Ω·cm at 700° C. and may be useful as a material for an electrostatic chuck in such a high temperature range. That is, in an electrostatic chuck utilizing Johnson-Rahbec force, it is desired to adjust the volume resistivity of a material for a substrate at a value not lower than 1×10⁸ Ω·cm and not higher than 1×10¹³ Ω·cm for obtaining a high chucking force and improved response. On this viewpoint, the aluminum nitride ceramics according to the present invention has a volume resistivity in the range described above at a temperature range of for example 300 to 800° C. and particularly 400 to 700° C. The ceramics is thus useful as a material for an electrostatic chuck designed for use in such high temperature range. Further, the ceramics has a high volume resistivity at room temperature and useful as a material for an electrostatic chuck utilizing Coulomb force.

EXAMPLES

[0069] (1) Production of Mixed Powder of AlN/B₄C/Y₂O₃

[0070] Commercial AlN powder produced by reduction nitriding or gaseous phase synthesis was used. Commercial B₄C powder having a high purity and a mean particle diameter of not larger than 2 μm was used. Commercial powder of Y₂O₃ with a purity of not lower than 99.9 percent and a mean particle diameter of not larger than 1 μm was used.

[0071] Each powder was weighed as shown in tables 1 and 3. The amounts of B₄C and Y₂O₃ were converted to weight parts provided that the amount of aluminum nitride was converted to 100 weight parts. Each weighed powder was then subjected to wet blending using isopropyl alcohol as a solvent, a nylon pot and nylon balls for 4 hours to obtain slurry. After the blending, the slurry was collected and dried at 110° C. in nitrogen atmosphere to obtain powdery raw material. The amounts of AlN, B₄C and Y₂O₃ in the formulation were calculated as “weight parts” ignoring the contents of impurities in each powder.

[0072] (2) Forming and Sintering Steps

[0073] Each mixed powder obtained in (1) section was then formed by uniaxial pressing at a pressure of 200 kgf/cm² to obtain a disk-formed body with a diameter of about 50 mm and a thickness of about 20 mm, which was then contained in a mold made of graphite for sintering.

[0074] Each formed body was sintered by hot pressing at a pressure of 200 kgf/cm² and a maximum temperature of 1800 to 2000° C. for 4 hours and then cooled. In some examples, a temperature holding step was introduced before reaching the maximum sintering temperature. Temperature was held at 1500 or 1600 or 1700° C. for 20 hours in the holding step. During the sintering, the formed body was set in vacuum from room temperature to 1000° C. and then nitrogen gas was introduced at a pressure of 1.5 kgf/cm² from 1000° C. to each sintering (maximum) temperature shown in the tables.

[0075] (3) Evaluation

[0076] The obtained sintered bodies were subjected to the following evaluation.

[0077] (Density, Open Porosity)

[0078] They are measured by Archimedes' method using water as a medium.

[0079] (Relative Density)

[0080] Relative density was calculated by the following formula.

(Bulk density)×100/(Theoretical density calculated based on the composition of the mixed raw material)

[0081] (Volume Resistivity)

[0082] It is measured by a method according to “JIS C 2141” from room temperature to about 700° C. under vacuum. The test sample has the following parts: a circular plate with a diameter φ of 50 mm and thickness of 1 mm; a main electrode with a diameter of 20 mm; a guard electrode with an inner diameter of 30 mm and outer diameter of 40 mm; and an applying electrode with a diameter of 45 mm. The electrodes are formed of silver. 500 V/mm of voltage is applied and a current is read one minute after the application of voltage so that the volume resistivity is calculated.

[0083] (Bending Strength)

[0084] A four-point bending strength at room temperature is measured according to “JIS R1601”.

[0085] (Thermal Conductivity)

[0086] Thermal conductivity was measured by laser flash method and calculated. The specific heat value (753 J/kg·K) of aluminum nitride was used for the calculation.

[0087] (Lattice Constants)

[0088] It was measured by WPPD method applying known lattice constants of Al₂O₃ as an internal standard. The measurements was performed using a rotating anode type X-ray diffraction system “RINT” supplied by “Rigaku Denki” under the following conditions: CuK α1 (monochromatized by Ge incident monochrometer), 50 kV, 300 mA, and 2θ=30 to 120°.

[0089] (Contents of B and Y)

[0090] They are determined by inductively coupled plasma (ICP) spectrometry.

[0091] (Oxygen and Nitrogen Contents)

[0092] They are determined by inert gas melting infrared absorptiometry analysis method.

[0093] (Carbon Content: “b” Weight Percent)

[0094] It is determined by high frequency heating infrared absorptiometry analysis method.

[0095] (Crystalline Phase)

[0096] It is determined by a rotating anode type X-ray diffraction system “RINT” supplied by “Rigaku Denki” under the following condition: CuKα, 50 kV, 300 mA, and 2θ=10 to 70°.

[0097] (Observation of Microstructure)

[0098] The distribution of each element was analyzed by EPMA.

[0099] (Oxygen Content in Aluminum Nitride Grains: “a” Weight Percent)

[0100] The total oxygen content in each sintered body was measured by chemical analysis. The content of Y was determined by inductively coupled plasma (ICP) spectrometry. The Y content is converted to the content of Y₂O₃ so that the content in Y₂O₃ was calculated. The oxygen content in Y₂O₃ was subtracted from the total content (obtained by chemical analysis) in each sintered body to obtain a calculated oxygen content (“a” weight percent) in grains.

[0101] (a/b)

[0102] The carbon content (“b” weight percent) in each sintered body was determined by high frequency heating infrared absorptiometry analysis method. The “a” value is divided by the “b” value. TABLE 1 sintering condition B4C Y203 holding step properties of sintered body amount amount maximum before resistivity 500° C. added added tempera- hold sintering at open apparent bulk relative at room resist- 600° C. 700° C. exam- parts by parts by ture ing maximum porosity density density density temperature ivity resistivity resistivity ple weight weight ° C. time temperature % g/cm3 g/cm3 % Ω · cm Ω · cm Ω · cm Ω · cm 1 3.4 2 2000 4 1500° C. × 0.02 3.19 3.19 98.2 3E+15 1E+10 1E+09 2E+08 20 hr 2 3.4 2 2000 4 None 0.01 3.20 3.20 98.5 5E+15 3E+10 3E+09 4E+08 3 2.3 2 2000 4 None 0.00 3.23 3.23 99.0 4E+15 1E+11 9E+10 9E+08 4 1.1 2 2000 4 None 0.01 3.24 3.24 99.1 5E+15 7E+08 4E+07 8E+06 5 5.7 2 2000 4 None 0.00 3.17 3.17 98.3 2E+15 6E+09 6E+08 8E+07 6 3.4 0 2000 4 1500° C. × 0.03 3.17 3.17 98.2 2E+15 2E+10 2E+09 2E+08 20 hr 7 3.4 2 1800 4 1500° C. × 0.01 3.19 3.19 98.0 2E+15 5E+10 5E+09 6E+08 20 hr 8 3.4 5 2000 4 None 0.01 3.23 3.23 98.4 6E+14 4E+09 4E+08 6E+07 9 3.4 0 2000 4 1700° C. × 0.02 3.13 3.13 96.9 8E+14 4E+09 4E+08 3E+07 20 hr

[0103] TABLE 2 oxygen thermal thermal lattice lattice content in identified bending conduct diffusivity constant constant properties of sintered body grains intergranular phase strength ivity ×1e−5 a-axis c-axis (weight percent %) weight YAL:YAlO3 example MPa W/mK m2/s A A B N O C Y C/B percent % a/b YAM:Y4Al2O9 1 325 58 2.4 3.1146 4.9832 2.39 32.7 0.92 0.63 1.09 0.26 0.63 0.99 BN, YB4 2 376 43 1.8 3.1158 4.9827 2.44 31.14 1.09 0.757 1.45 0.31 0.70 0.92 BN, YB4, YB6, 3 308 56 2.3 3.1143 4.9829 1.67 32.26 1.08 0.553 1.38 0.33 0.71 1.28 BN, YB4 4 303 78 3.2 3.1131 4.9822 0.83 32.83 0.84 0.336 0.88 0.40 060 179 BN, YB4, YAL 5 361 42 1.7 3.1163 4.9841 3.95 30.8 1.09 1.2 1.2 0.30 0.77 0.64 BN, YB4 6 324 52 2.2 3.1151 4.9820 2.56 32.66 0.73 0.796 — 0.31 0.73 0.92 BN, B4C 7 511 46 1.9 — — — — — — — — — — BN, YB4 8 298 50 2.0 — — — — — — — — — — BN, YB4, YAL 9 433 99 4.2 — — — — — — — — — — BN

[0104] TABLE 3 sintering condition B4C Y203 holding step properties of sintered body amount amount maximum before resistivity 500° C. 600° C. 700° C. added added tempera- hold sintering at open apparent bulk relative at room resist- resist- resist- parts by parts by ture ing maximum porosity density density density temperature ivity ivity ivity weight weight ° C. time temperature % g/cm3 g/cm3 % Ω · cm Ω · cm Ω · cm Ω · cm example 10 1.1 2 2000 4 None 0.00 3.25 3.25 99.4 5E+15 4E+10 4E+9  5E+8  example 11 1.1 2 1900 4 1600° C. × 0.04 3.24 3.24 99.0 1E+16 4E+10 4E+9  4E+8  20 hr comparative 0   0 1900 4 None 0.03 3.27 3.27 100.2 5E+12 2E+05 — — example 1 comparative 0.6 2 2000 4 None 0.01 3.25 3.25 99.3 2E+15 5E+07 5E+06 7E+05 example 2 B4C comparative 8.5 2 2000 4 None 0.02 3.16 3.16 99.1 1E+15 2E+06 1E+05 — example 3 BN comparative 0.6 2 2000 4 1500° C. × 0.02 3.26 3.25 99.4 4E+14 6E+06 2E+05 — example 4 C 20 hr comparative 0   5 1900 4 None 0.07 3.31 3.31 99.8 2E+15 5E+07 2E+06 — example 5

[0105] TABLE 4 thermal thermal diffusivi lattice lattice bending conduct ty constant constant properties of sintered body oxygen identified strength ivity ×1e−5 a-axis c-axis (weight percent %) content intergranular MPa W/mK m2/s A A B N O C Y C/B in grains a/b phase example 367  92 3.8 3.1129 4.9817 0.79 33.05 0.58 0.323 1.06 0.41 0.29 0.91 — 10 example 390 114 4.7 3.1123 4.9813 0.82 33.48 0.61 0.235 1.34 0.29 0.25 1.06 — 11 comparative 400 96 3.9 3.1117 4.9783 — 33.59 0.67 0.03 — — — — Al203 example 1 comparative 327 103 4.2 3.1123 4.9808 — — — — — — — — BN, YAL example 2 comparative 382 113 4.5 3.1115 4.9808 3.35 35.19 1.22 0.02 1.55 0.01 — — BN, YAL example 3 comparative 361 163 6.7 3.1118 4.9808 — — 0.73 0.57 0.93 — — — YAL example 4 comparative 439 174 7.9 3.1117 4.9804 — 32.25 1.48 0.024 2.73 — — — YAL, YAM example 5

[0106] The experimental results will be studied.

Example 1

[0107] Commercial AlN powder (oxygen content is 0.97 percent) produced by reduction nitriding was used. The powdery raw material has a composition of 100/3.4/2 (AlN/B₄C/Y₂O₃; weight parts). The raw material was formed and sintered. In the sintering step, the temperature was elevated at a speed of 1000° C./hour, held at 1500° C. for 20 hours and held at 2000° C. for 4 hours to obtain a dense body having a density of 3.19 g/cm³ and an open porosity of 0.02 percent.

[0108] The resulting sample has volume resistivities of 3×10¹⁵ Ω·cm at room temperature (25° C.), 1×10¹⁰ Ω·cm at 500° C. and 2×10⁸ Ω·cm at 700° C. Abbreviation was applied in the tables for describing a value of volume resistivity as follows. For example, “3×10¹⁵”Ω·cm is described as “3E+15” Ω·cm.

[0109]FIG. 1 is a graph showing the dependency of volume resistivity on temperature of the sample according to example 1. The properties of the samples according to example 3 and comparative example 1 are also shown in FIG. 1. The materials according to the present invention have a higher volume resistivity at any temperature, especially at a high temperature range, compared with the conventional material.

[0110] The sample according to example 1 has a high strength of 325 MPa and a thermal conductivity of 58 W/m·K. It is speculated that the thermal conductivity is reduced due to much atoms solid-soluted into AlN grains. According to X-ray diffraction analysis, AlN, BN and YB₄ phases are identified.

[0111] The distribution of B, C, O, N and Y atoms in the sintered body taken by EPMA is shown in FIG. 2. FIG. 3 shows the distribution in the sample according to comparative example 5 as a reference. In the figures, more atoms are present as the brightness higher (refer to a color tone scale in the right column). As shown in FIG. 2, in the example 1, it is proved that much C and O atoms are present in AlN grains. B atoms are not considerably solid-soluted into the AlN grains. In the inventive sample, C and O atoms are solid-soluted into the AlN grains to provide a higher volume resistivity. The mechanism of an increase of the volume resistivity due to the solid-soluted C and O atoms into AlN grains is not clear. C and O atoms may be solid-soluted into AlN grains to reduce the carrier density or to generate crystalline defects prohibiting the transfer of the carriers.

[0112] The lattice constants of AlN of the sample according to example 1 were shown in table 1 and FIG. 4. In the sample according to example 1, both of “a” and “c” axes are considerably expanded compared with those of a conventional sample, indicating the presence of atoms solid-soluted into AlN grains. The solid-soluted atoms are proved to be C and O atoms according to EPMA.

Examples 2 to 9

[0113] Commercial AlN powder (oxygen content of 0.97 percent) produced by reduction nitriding was used. In example 2, the composition of powdery raw material was the same as example 1, but the temperature holding step at 1500° C. was omitted. In this case, the volume resistivity of the sample was not substantially changed and thermal conductivity was slightly reduced compared with those in example 1. The temperature holding step provides a higher thermal conductivity. However, a holding step at about 1600° C. for a long time period may result in continuous intergranular phase that mainly consists of boron nitride containing carbon, so that the volume resistivity may be reduced. It is necessary to avoid such reduction of volume resistivity when the temperature holding step is performed.

[0114] In examples 3 and 4, the manufacturing conditions and added amounts of yttria were the same as in the example 2 except that the content of B₄C was reduced. It is possible to obtain a material having a high resistivity and thermal conductivity even when the content of B₄C was reduced.

[0115] In example 5, the manufacturing conditions and added amounts of yttria were the same as in the examples 2, 3 and 4 except that the added amount of B₄C was increased. It is possible to obtain a material having a high resistivity. The volume resistivity is not substantially changed and thermal conductivity is reduced by increasing the added amount of B₄C.

[0116] In example 6, the manufacturing conditions and added amounts of B₄C were the same as in the example 2 except that yttria was not added. It is possible to obtain a material having a high resistivity when a rare earth element is not added. A maximum sintering temperature of about 2000° C. is necessary to sufficiently densify the sintered body so that a production cost is increased.

[0117] In example 7, the added amount of B₄C was the same as in the example 6 but 2 weight percent of yttria was added. In this example, liquid phase is generated during the sintering step to reduce the maximum sintering temperature required for sufficient densification to a temperature of about 1800° C.

[0118] In example 8, the added amount of B₄C and sintering conditions were the same as in the example 2 except that the added amount of yttria was increased to 5 weight percent. It is thereby possible to increase the volume resistivity compared with the sample having a lower added amount of Y₂O₃ (example 2).

[0119] In example 9, the sintering temperature and the composition of powdery raw material were the same as those in the example 6, and the temperature was maintained at 1700° C. in the temperature holding step. The resulting sample has a higher thermal conductivity compared with the sample according to the example 1 in which temperature is maintained at 1500° C.

Examples 10 and 11

[0120] Commercial AlN powder (oxygen content of 0.44 percent) produced by gaseous phase process was used. In examples 10 and 11, the AlN powder having a lower oxygen content was used so that the thermal conductivity was considerably improved to 92 or 114 W/mK. In the examples 10 and 11, the oxygen content in grains are not higher than 0.5 weight percent. On the contrary, in the example 1 to 6, the oxygen content in grains are relatively large. The oxygen content in grains and thermal conductivity are thus clearly correlated with each other.

[0121] Further in the examples 1 to 11, a/c is within 0.25 to 2.0.

Comparative Examples 1 to 5

[0122] Commercial AlN powder produced by reduction nitriding (oxygen content of 0.97 percent) was used. The comparative example 1 provides an AlN sintered body without additives. As shown in FIG. 4, the lattice constants of AlN lattices are not so different to JCPDS values (No. 25-1133) and substantially smaller than those in the examples. Smaller amounts of C and O atoms are solid-soluted into AlN grains compared with the inventive examples, resulting in a lower volume resistivity.

[0123] In comparative example 2, the composition of powdery raw material is 100/0.6/2 (AlN/B₄C/Y₂O₃; weight parts). The added amount of B₄C was reduced in this example. Although the lattice parameters of AlN lattices are changed to a some degree compared with JCPDS values, amounts of C and O atoms solid-soluted into AlN grains are not sufficient, resulting in a reduced volume resistivity.

[0124] In comparative example 3, commercial BN powder was used instead of B₄C to evaluate the properties of the resulting sintered body. The composition of powdery raw material was 100/8.5/2 (AlN/BN/Y₂O₃; weight parts). BN and YAlO₃ phases are present other than AlN phase. Such crystalline phases are similar to those shown in the above samples according to the inventive examples with B₄C added. Although the amount of added BN is 8.5 weight percent and considerably larger, the resistivity at 500° C. is as low as 2×10⁶ Ω·cm. The lattice constants of AlN lattice are not substantially changed compared with JCPDS values. The content of atoms solid-soluted into AlN grains is small.

[0125] In comparative example 4, commercial carbon powder with a high purity was used. The properties of the resulting sintered body were measured for comparison. The composition of powdery raw material was 100/0.6/2 (AlN/C/Y₂O₃; weight parts). The volume resistivity at 500° C. is as low as 6×10⁶ Ω·cm. The thermal conductivity is as high as 163 W/m·K and the differences between the lattice constants and JCPDS values are small. It is thus considered that C atoms are not easily solid-soluted into AlN grains in the case of adding carbon powder.

[0126] Comparative example 5 provides a conventional AlN material as a reference material for EPMA measurement. Y₂O₃ is added in the AlN material. The thermal conductivity is as high as 174 W/m·K and the differences between the lattice constants of AlN lattice and JCPDS values are small. As shown in an EPMA image in FIG. 3, only small amounts of C and O atoms are solid-soluted into AlN grains.

[0127] As described above, the present invention provides an aluminum ceramics having an increased volume resistivity.

[0128] The present invention has been explained referring to the preferred embodiments. However, the present invention is not limited to the illustrated embodiments which are given by way of examples only, and may be carried out in various modes without departing from the scope of the invention. 

1. An aluminum nitride ceramics containing 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms and having a volume resistivity at room temperature of not lower than 1×10¹⁴ Ω·cm.
 2. The ceramics of claim 1 having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.
 3. The ceramics of claim 1, wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.
 4. The ceramics of claim 1 having a weight ratio of carbon atoms to boron atoms (C/B) of 0.1 to 0.5.
 5. The ceramics of claim 1 having a volume resistivity at 700° C. of not lower than 1×10⁷ Ω·cm.
 6. The ceramics of claim 1 containing 0.1 to 10 weight percent of a rare earth element.
 7. The ceramics of claim 1 having an open porosity of not higher than 0.1 percent.
 8. The ceramics of claim 1 having a thermal conductivity of not lower than 30 W/m·K.
 9. The ceramics of claim 1 being a sintered body.
 10. The ceramics of claim 9 having intergranular phase mainly consisting of boron nitride.
 11. The ceramics of claim 1, wherein a ratio (a/b) of a content of oxygen (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in said ceramics is not lower than 0.25 and not higher than 2.0.
 12. The ceramics of claim 1 having a content of oxygen solid-soluted into aluminum nitride grains of not higher than 0.5 percent.
 13. A member for use in a system for producing semiconductors comprising said ceramics of claim
 1. 14. An corrosion resistant member comprising said ceramics of claim
 1. 15. An aluminum nitride ceramics containing 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms and having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.
 16. The ceramics of claim 15, wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.
 17. The ceramics of claim 15 having a weight ratio of carbon atoms to boron atoms (C/B) of 0.1 to 0.5.
 18. The ceramics of claim 15 having a volume resistivity at 700° C. of not lower than 1×10⁷ Ω·cm.
 19. The ceramics of claim 15 containing 0.1 to 10 weight percent of a rare earth element.
 20. The ceramics of claim 15 having an open porosity of not higher than 0.1 percent.
 21. The ceramics of claim 15 having a thermal conductivity of not lower than 30 W/m·K.
 22. The ceramics of claim 15 being a sintered body.
 23. The ceramics of claim 22 having intergranular phase mainly consisting of boron nitride.
 24. The ceramics of claim 15, wherein a ratio (a/b) of a content of oxygen (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in said ceramics is not lower than 0.25 and not higher than 2.0.
 25. The ceramics of claim 15 having a content of oxygen solid-soluted into aluminum nitride grains of not higher than 0.5 percent.
 26. A member for use in a system for producing semiconductors comprising said ceramics of claim
 15. 27. An corrosion resistant member comprising said ceramics of claim
 15. 28. An aluminum nitride ceramics containing 0.5 to 10 weight percent of boron atoms and 0.1 to 2.5 weight percent of carbon atoms, wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.
 29. The ceramics of claim 28 having a weight ratio of carbon atoms to boron atoms (C/B) of 0.1 to 0.5.
 30. The ceramics of claim 28 containing 0.1 to 10 weight percent of a rare earth element.
 31. The ceramics of claim 28 having an open porosity of not higher than 0.1 percent.
 32. The ceramics of claim 28 having a thermal conductivity of not lower than 30 W/m·K.
 33. The ceramics of claim 28 being a sintered body.
 34. The ceramics of claim 33 having intergranular phase mainly consisting of boron nitride.
 35. The ceramics of claim 28, wherein a ratio (a/b) of a content of oxygen (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in said ceramics is not lower than 0.25 and not higher than 2.0.
 36. The ceramics of claim 28 having a content of oxygen solid-soluted into aluminum nitride grains of not higher than 0.5 percent.
 37. A member for use in a system for producing semiconductors comprising said ceramics of claim
 28. 38. An corrosion resistant member comprising said ceramics of claim
 28. 39. An aluminum nitride ceramics being produced by sintering a mixture containing at least aluminum nitride and boron carbide and having a volume resistivity at room temperature of not lower than 1×10¹⁴ Ω·cm.
 40. The ceramics of claim 39 having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.
 41. The ceramics of claim 39, wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.
 42. The ceramics of claim 39 having a weight ratio of carbon atoms to boron atoms (C/B) of 0.1 to 0.5.
 43. The ceramics of claim 39 containing 0.1 to 10 weight percent of a rare earth element.
 44. The ceramics of claim 39 being a sintered body.
 45. The ceramics of claim 44 having intergranular phase mainly consisting of boron nitride.
 46. The ceramics of claim 39, wherein a ratio (a/b) of a content of oxygen (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in said ceramics is not lower than 0.25 and not higher than 2.0.
 47. The ceramics of claim 39 having a content of oxygen solid-soluted into aluminum nitride grains of not higher than 0.5 percent.
 48. A member for use in a system for producing semiconductors comprising said ceramics of claim
 39. 49. An corrosion resistant member comprising said ceramics of claim
 39. 50. An aluminum nitride series ceramics being produced by sintering a mixture containing at least aluminum nitride and boron carbide and having a volume resistivity at 500° C. of not lower than 1×10⁸ Ω·cm.
 51. The ceramics of claim 50, wherein an a-axis lattice constant of aluminum nitride is not shorter than 3.112 angstrom and a c-axis lattice constant of aluminum nitride is not shorter than 4.980 angstrom.
 52. The ceramics of claim 50 having a weight ratio of carbon atoms to boron atoms (C/B) of 0.1 to 0.5.
 53. The ceramics of claim 50 containing 0.1 to 10 weight percent of a rare earth element.
 54. The ceramics of claim 50 being a sintered body.
 55. The ceramics of claim 54 having intergranular phase mainly consisting of boron nitride.
 56. The ceramics of claim 50, wherein a ratio (a/b) of a content of oxygen (“a” weight percent) solid-soluted in aluminum nitride grains to a carbon content (“b” weight percent) in said ceramics is not lower than 0.25 and not higher than 2.0.
 57. The ceramics of claim 50 having a content of oxygen solid-soluted into aluminum nitride grains of not higher than 0.5 percent.
 58. A member for use in a system for producing semiconductors comprising said ceramics of claim
 50. 